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Thermodynamics and Electronic Properties of Heterometallic Multinuclear Actinide-Containing Metal−Organic Frameworks with “Structural Memory”

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Otega A. Ejegbavwo,† Corey R. Martin,† Oyindamola A. Olorunfemi,† Gabrielle A. Leith,† Richard T. Ly,† Allison M. Rice,† Ekaterina A. Dolgopolova,† Mark D. Smith,† Stavros G. Karakalos,‡ Nancy Birkner,§,⊥ Brian A. Powell,∥ Shubham Pandey,∇ Robert J. Koch,○ Scott T. Misture,○ Hans-Conrad zur Loye,† Simon R. Phillpot,∇ Kyle S. Brinkman,§,⊥ and Natalia B. Shustova*,† †

Department of Chemistry and Biochemistry, University of South Carolina, Columbia, South Carolina 29208, United States College of Engineering and Computing, University of South Carolina, Columbia, South Carolina 29208, United States § Department of Materials Science and Engineering, Clemson University, Clemson, South Carolina 29634, United States ∥ Department of Environmental Engineering and Earth Science, Clemson University, Clemson, South Carolina 29634, United States ⊥ Center for Nuclear Environmental Engineering Sciences and Radioactive Waste Management (NEESRWM), Clemson University, Clemson, South Carolina 29634, United States ∇ Department of Materials Science and Engineering, University of Florida, Gainesville, Florida 32611, United States ○ Kazuo Inamori School of Ceramic Engineering, Alfred University, Alfred, New York 14802, United States ‡

S Supporting Information *

ABSTRACT: Thermodynamic studies of actinide-containing metal−organic frameworks (An-MOFs), reported herein for the first time, are a step toward addressing challenges related to effective nuclear waste administration. In addition to An-MOF thermochemistry, enthalpies of formation were determined for the organic linkers, 2,2′-dimethylbiphenyl-4,4′-dicarboxylic acid (H 2 Me 2 BPDC) and biphenyl-4,4′-dicarboxylic acid (H2BPDC), which are commonly used building blocks for MOF preparation. The electronic structure of the first example of An-MOF with mixed-metal AnAn′-nodes was influenced through coordination of transition metals as shown by the density of states near the Fermi edge, changes in the Tauc plot, conductivity measurements, and theoretical calculations. The “structural memory” effect (i.e., solvent-directed crystalline−amorphous−crystalline structural dynamism) was demonstrated as a function of node coordination degree, which is the number of organic linkers per metal node. Remarkable three-month water stability was reported for Th-containing frameworks herein, and the mechanism is also considered for improvement of the behavior of a U-based framework in water. Mechanistic aspects of capping linker installation were highlighted through crystallographic characterization of the intermediate, and theoretical calculations of free energies of formation (ΔGf) for U- and Th-MOFs with 10- and 12-coordinated secondary building units (SBUs) were performed to elucidate experimentally observed transformations during the installation processes. Overall, these results are the first thermochemical, electronic, and mechanistic insights for a relatively young class of actinide-containing frameworks.

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minimal structural density.13−21 However, the field of actinide-based MOFs,22 especially in comparison with nonactinide-containing frameworks,23−27 suffers from the fact that fundamental properties including thermodynamics, electronics, or detailed photophysics have not been investigated. Herein, we report (i) the first thermochemical studies performed for any An-based MOFs including several examples

INTRODUCTION

The stability of actinide-containing architectures and their chemical interactions with the environment have been increasingly studied over the past decades because of their significance for nuclear waste administration.1−4 Due to their modularity, structural versatility, high porosity, and high tunability, metal−organic frameworks (MOFs)5−9 have been utilized as a platform for nuclear waste sequestration10 and actinide immobilization,11 resulting in the development of materials12 with a high actinide content and possessing © XXXX American Chemical Society

Received: May 2, 2019 Published: June 20, 2019 A

DOI: 10.1021/jacs.9b04737 J. Am. Chem. Soc. XXXX, XXX, XXX−XXX

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Journal of the American Chemical Society of the common organic linkers, (ii) the first example of heterometallic multinuclear An-MOF nodes with a coordinated transition metal and the first electronic structure studies using density of states (DOS) and conductivity measurements, (iii) over three-month water stability of a Th-MOF, (iv) structural “crystalline−amorphous−crystalline” cycling of AnMOFs as a function of metal node geometry, and (v) theoretical studies establishing the dependence of An-MOF stability on the nature of linker connectivity to the secondary building unit (SBU, Scheme 1). In addition, novel actinideScheme 1. Overview of the Presented Results: Thermodynamics, Electronic Structure, and “Structural Memory” Effect of An-MOFs

containing frameworks, M-Linker-n, (M (Th, U) = a metal in the node, Linker = an organic linker, and n = number of carboxylic groups attached to a metal node) such as Th6O4(OH)4(NO3)2(Me2BPDC)5 (Th6-Me2BPDC-NO3-10; Me2BPDC2− = 2,2′-dimethylbiphenyl-4,4′-dicarboxylate), Th 6 O 4 (OH) 8 (Me 2 BPDC) 4 (Th 6 -Me 2 BPDC-8), and U6O4(OH)4(TFA)2(Me2BPDC)5 (U6-Me2BPDC-TFA-10, TFA = trifluoroacetate, Figures 1 and S4), were prepared. The discussion in this paper will be organized in the following order: synthetic details and chemical stability of the An-MOFs, their thermochemical studies including the measurements for organic linkers, analysis of the electronic structure of the heterometallic An-MOFs, “structural memory” effect of An-MOFs (i.e., solvent-directed crystalline−amorphous−crystalline cycling as a function of metal node geometry), and mechanistic insights on the capping linker installation process (i.e., postsynthetic linker coordination to framework metal nodes). The comprehensive analysis of AnMOFs includes single-crystal and powder X-ray diffraction (PXRD), inductively coupled plasma mass spectrometry (ICPMS), conductivity, solution calorimetric measurements, thermogravimetric analysis, nuclear magnetic resonance (NMR), Fourier transform infrared (FTIR), and X-ray photoelectron spectroscopies (XPS), as well as theoretical modeling.

Figure 1. (top) Two views of secondary building units: 8-coordinated (top), 10-coordinated (middle), and 12-coordinated metal nodes (bottom). (bottom, lef t) PXRD patterns of U6-Me2BPDC-8 (simulated),3 Th6-Me2BPDC-8a (experimental), Th6-Me2BPDC-8b (simulated), and Th6-Me2BPDC-8a in water (experimental). (bottom, right) X-ray crystal structure of Th6-Me2BPDC-8b. The teal, red, and gray spheres represent Th, O, and C atoms, respectively. Hydrogen atoms and solvents molecules were omitted for clarity.

below). The presence of labile nitrate groups coordinated to the equatorial position of metal nodes allowed us to perform postsynthetic linker installation as described below (Figure 6). The Th6O4(OH)4(BPDC)6(DMF)6 MOF (Th6-BPDC-12; BPDC2− = biphenyl-4,4′-dicarboxylate) was prepared by heating Th(NO3)4·H2O and H2BPDC in DMF at 120 °C for 72 h. Modification of the synthetic conditions by increasing the molar ratio of metal salt to linker used for Th6-Me2BPDCNO3-10 preparation allowed us to reduce the “metal-nodesaturation degree” resulting in the synthesis of Th6-Me2BPDC8 with eight linkers per metal node versus ten Me2BPDC2− observed for Th6-Me2BPDC-NO3-10. Unsaturated nodes (i.e., with a number of linkers 95%, International Bio-Analytical Industries Inc.), ThCl4 (>95%, International Bio-Analytical Industries Inc.), Th(NO3)4·H2O (99.8%, Strem Chemicals Inc.), ZrCl4 (99.5%, Alfa Aesar), Co(NO3)2·6H2O (99%, Strem Chemicals Inc.), potassium acetate (lab grade, Ward’s Science), K2CO3 (lab grade, Ward’s Science), 1,4-dibromobenzene (98%, Sigma-Aldrich), 4-methoxycarbonylphenylboronic acid (>97%, Boronic Molecular), 1,4-benzenedicarboxylic acid (99%, TCI chemicals), biphenyl-4,4′-dicarboxylic acid (97%, Oakwood Chemical), Pd(PPh3)4 (96%, Matrix Scientific), methyl-(4-iodo-3)-methylbenzoate (98%, BeanTown Chemical), 4,4′diiodobiphenyl (98%, Matrix Scientific), 4,4,4′,4′,5,5,5′,5′-octamethyl-2,2′-bi-(1,3,2-dioxaborolane) (>98%, Ark Pharm), PdCl2(PPh3)2 (96%, Oakwood Chemical), CsF (99%, Oakwood Chemical), KOH (ACS grade, Fisher Chemical), 2,5-dibromoaniline (97%, Oakwood Chemical), Pd(OAc)2 (>95%, Ox-Chem), trifluoroacetic acid (99%, Sigma-Aldrich), nitric acid (70%, Sigma-Aldrich), tetrahydrofuran (ACS grade, Macron Fine Chemicals), dichloromethane (ACS grade, H

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PXRD studies were used to monitor sample crystallinity (Figures S19, S22−S26). General Linker Installation Procedure. Crystals of Th6Me2BPDC-NO3-10 or Th6-Me2BPDC-8 MOFs were soaked in 0.5 mL of the corresponding linker solution in DMF and heated at 75 °C in a preheated isothermal oven. The obtained crystals were collected by filtration and thoroughly washed with DMF using the Soxhlet extraction procedure. The samples were analyzed by single-crystal or powder X-ray diffraction. The linker installation was confirmed by 1H NMR spectroscopy as described below. Digestion Procedure. To study the linker composition of the synthesized MOFs by 1H NMR spectroscopy, a mixture of 500 μL of DMSO-d6 and 3 μL of concentrated HCl was added to 5 mg of thoroughly washed material (washing was done in DMF using the Soxhlet extraction method), followed by mild heating of the mixture to ensure complete dissolution of sample. The percent of linker installed was calculated based on linker ratios found in the 1H NMR spectra of the digested samples. The amount of linker installed can be calculated from geometrical analysis of the parent MOF structure and length of the corresponding linker as shown by Zhou and coworkers.52 Synthesis and Characterization of Th6-Me2BPDC(Me2TPDC)12. Crystals of Th6-Me2BPDC-NO3-10 (5.0 mg, 1.6 μmol) were heated in 0.5 mL of 15 mM H2Me2TPDC solution in DMF at 75 °C in a preheated isothermal oven for 24 h. This procedure resulted in the Th6-Me2BPDC-8 intermediate MOF as confirmed by singlecrystal X-ray crystallography. The crystals of the Th6-Me2BPDC-8 intermediate were then heated for an additional 48 h in the presence of 0.5 mL of a 0.16 M H2Me2BPDC DMF solution. After that, the formed Th6-Me2BPDC(Me2TPDC)-12 crystals were thoroughly washed with DMF to remove any residual linker. The crystals were suitable for single-crystal X-ray studies. Detailed description of the data collection and refinement details is given in the Supporting Information. Table S6 contains the crystallographic refinement data of the Th6-Me2BPDC-8 intermediate and Th6-Me2BPDC(Me2TPDC)12 crystals. PXRD studies were used to confirm the preserved framework integrity of the MOFs at every stage of the installation process (Figure S31). Based on 1H NMR studies, the percentage of the installed linker is given in Table S9. The 1H NMR spectrum is shown in Figure S34. Attempts of H2Me2BPDC and H2QPDC Installation into Th6Me2BPDC-NO3-10. Crystals of Th6-Me2BPDC-NO3-10 (5.0 mg, 1.6 μmol) were heated in 0.5 mL of 0.16 M H2Me2BPDC solution in DMF at 75 °C in a preheated isothermal oven for 72 h. After that, crystals were thoroughly washed with DMF to remove any residual linker. Single-crystal X-ray studies of the crystals revealed no structural changes in the Th6-Me2BPDC-NO3-10 structure. Based on the different orientation of adjacent metal nodes, the 12-coordinated MOF cannot be prepared through the installation of the H2Me2BPDC linker in the Th6-Me2BPDC-10 structure. Detailed description of the data collection and refinement details is given in the Supporting Information. Table S7 contains the crystallographic refinement data. Crystals of Th6-Me2BPDC-NO3-10 (5.0 mg, 1.6 μmol) were heated in 0.5 mL of 15 mM H2QPDC solution in DMF at 75 °C in a preheated isothermal oven for 72 h. After heating, crystals were thoroughly washed with DMF to remove any residual linker. Singlecrystal X-ray studies of the residual crystals revealed no structural changes in the Th6-Me2BPDC-NO3-10 structure. Detailed description of the data collection and refinement details is in the Supporting Information. Table S7 contains the crystallographic refinement data. Synthesis and Characterization of Th6-Me2BPDC(BDC)-10. Crystals of Th6-Me2BPDC-NO3-10 (5.0 mg, 1.6 μmol) were heated in 0.5 mL of 0.16 M H2BDC solution in DMF at 75 °C in a preheated isothermal oven for 24 h. After the installation process, the MOF was thoroughly washed with DMF to remove any residual linker. The crystals were unsuitable for single-crystal X-ray studies; however, PXRD studies were used to confirm the preserved framework integrity (Figure S31). Based on 1H NMR studies, the percentage of the installed linker is given in Table S9, and the 1H NMR spectrum is shown in Figure S35.

were suitable for single-crystal X-ray analysis. The single-crystal structure (Figure S27) and a detailed description of the data collection and refinement details are given in the Supporting Information. As shown in Figure S28, the PXRD pattern of assynthesized Th6-BPDC-12 matches the simulated pattern from the single-crystal X-ray data. PXRD studies were also used to confirm the crystallinity of the bulk material (Figure S28). The thermal stability of Th6-BPDC-12 was determined via thermogravimetric analysis (Figure S12). Preparation of U6-Me2BPDC-8-H2O-1d and U6Me2BPDC-8H2O-4d. The green crystals of U6-Me2BPDC-8 were washed once with DMF and soaked in water for 1 or 4 days at room temperature under an inert atmosphere. Detailed description of the data collection and refinement details is given in the Supporting Information. Table S4 contains the crystallographic refinement data. Synthesis and Characterization of U1.23Th4.77-Me2BPDC-8. The green crystals of U6-Me2BPDC-8 (42 mg) were washed once with DMF and soaked in a 1.0 mL solution of 0.17 M ThCl4 in DMF for 72 h at room temperature. After 72 h, the resulting crystals of U1.23Th4.77-Me2BPDC-8 (U/Th-8) were collected by centrifugation and washed thoroughly three times with DMF. The PXRD pattern of U1.23Th4.77-Me2BPDC-8 matches the simulated pattern. PXRD studies were used to confirm the crystallinity of the bulk material (Figure S14). IR (neat, cm−1): 3389, 2930, 1648, 1587, 1543, 1497, 1409, 1383, 1254, 1206, 1140, 1093, 1062, 1007, 916, 863, 838, 777, 731, 721, and 659 (Figure S17). The XPS spectra are shown in Figures 3 and S13. The Tauc plot is shown in Figure S14b, and the estimated band gap for the prepared heterometallic MOF was found to be 2.5 eV. Synthesis and Characterization of U1.23Th4.77Co3-Me2BPDC8. The prepared U1.23Th4.77-Me2BPDC-8 MOF (42.0 mg) was heated in a 0.25 M DMF solution (1.0 mL) of Co(NO3)2·6H2O for 48 h in a preheated oven at 75 °C. As a result of such treatment, the sample changed color from gray to dark yellow-green. After the synthesis of U1.23Th4.77-Me2BPDC-8, we employed a combination of PXRD to monitor the changes to the unit cell dimensions over 48 h, as well as XPS and Raman spectroscopies to determine the form of cobalt incorporated (Figures S14−S17). IR (neat, cm−1): 3424, 2930, 1649, 1586, 1542, 1482, 1409, 1296, 1253, 1207, 1093, 1062, 1020, 1032, 1007, 912, 863, 815, 778, 734, and 659 (Figure S17). PXRD patterns were measured every 6 h over 48 h to probe changes in unit cell parameters as a function of time, as well as to monitor the incorporation process (Figure S14a). A single peak was observed (6.4°, 2θ) with a decrease in intensity as the metal-node extension proceeded, while another peak (5.1°, 2θ) shifted to higher angles. We modeled this change and calculated the diffraction intensity changes as a function of the occupancy of the cobalt ion. Indeed, our simulated diffraction pattern shows a decrease in peak intensity as a function of the amount of cobalt ion incorporated, a result comparable to that obtained experimentally (Figure S14c). To determine that the cobalt ion was incorporated as a metal node extension and not included as a guest in the form of either Co(II) or Co(III) oxides, we performed Raman and XPS measurements. In the Raman spectra, there was no detection of the presence of either Co(II) or Co(III) oxides (Figure S17). Furthermore, XPS data of the Co(2p) region supported the Raman data (Figure S15). The PXRD studies did not reveal the presence of crystalline cobalt oxides. Conductivity measurements of the heterometallic MOFs were performed in a home-built in situ pressed-pellet device. The metal ratio in the sample, thoroughly washed for 1 week using the Soxhlet washing procedure to ensure removal of any residual metal salts, was determined by ICP-MS analysis technique. General Procedure To Study Structural Dynamism. The Th6Me2BPDC-NO3-10 and Th6-Me2BPDC-8 MOFs were soaked in 11 different solvents for 72 h during which the solvents were refreshed twice a day. Crystals suitable for single-crystal X-ray studies such as Th6-Me2BPDC-10-MeOH were analyzed. Detailed description of the data collection and refinement details of Th6-Me2BPDC-10-MeOH is given in the Supporting Information. Table S5 contains the crystallographic refinement data of Th6-Me2BPDC-10-MeOH. I

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Journal of the American Chemical Society Synthesis and Characterization of Th6-BPDC-10. Crystals of Th6-Me2BPDC-NO3-10 (5.0 mg, 1.6 μmol) were heated in 0.5 mL of 16 mM H2BPDC solution in DMF at 75 °C in a preheated isothermal oven for 48 h. After heating, crystals were thoroughly washed with DMF to remove any residual linker. Single-crystal X-ray studies of the obtained crystals demonstrate the Me2BPDC2−-to-BPDC2− linker replacement. Detailed description of the data collection and refinement details is given in the Supporting Information. Table S8 contains the crystallographic refinement data. PXRD studies were used to confirm the preserved framework integrity (Figure S32). Synthesis and Characterization of Th6-Me2BPDC(Me2TPDC)10. Th6-Me2BPDC-8 (5.0 mg, 1.8 μmol) was heated in 0.5 mL of 15 mM H2Me2TPDC solution in DMF at 75 °C in a preheated isothermal oven for 72 h. After the installation process, the Th6Me2BPDC(Me2TPDC)-10 MOF was thoroughly washed with DMF to remove any residual linker. PXRD studies were used to confirm the preserved framework integrity of the MOFs at every stage of the installation process, as well as ensure the phase purity of the bulk sample (Figure S30). Based on 1H NMR studies, the percentage of the installed linker is given in Table S9 and the spectrum is shown in Figure S37. Synthesis and Characterization of Th6-Me2BPDC(Me2BPDC)10. Th6-Me2BPDC-8 (5.0 mg, 1.8 μmol) was heated in 0.5 mL of 0.16 M H2Me2BPDC solution in DMF at 75 °C in a preheated isothermal oven for 72 h. After the installation process, the Th6Me2BPDC(Me2BPDC)-10 MOF was thoroughly washed with DMF to remove any residual linker. PXRD studies were used to confirm the preserved framework integrity of the MOFs at every stage of the installation process, as well as ensure the phase purity of the bulk sample (Figure S30). Synthesis and Characterization of Th6-Me2BPDC(BDC)-10. Th6-Me2BPDC-8 (5.0 mg, 1.8 μmol) was heated in 0.5 mL of 0.16 M H2BDC solution in DMF at 75 °C in a preheated isothermal oven for 24 h. After the installation process, the Th6-Me2BPDC(BDC)-10 MOF was thoroughly washed with DMF to remove any residual linker. PXRD studies were used to confirm the preserved framework integrity as well as ensure the phase purity of the bulk MOF sample (Figure S31). Based on 1H NMR studies, the percentage of the installed linker is given in Table S9. The 1H NMR spectrum is shown in Figure S38. Attempts of H2QPDC Installation into Th6-Me2BPDC-8. Th6Me2BPDC-8 (5.0 mg, 1.8 μmol) was heated in 0.5 mL of 15 mM H2QPDC solution in DMF at 75 °C in a preheated isothermal oven for 72 h. After the installation process, the MOF was thoroughly washed with DMF to remove any residual linker. PXRD and spectroscopic studies did not indicate successful linker installation (Figure S31). Physical Measurements. Single-crystal X-ray diffraction data were collected using a Bruker D8 QUEST diffractometer equipped with a PHOTON-100 CMOS area detector and an Incoatec microfocus source (Mo Kα radiation, λ = 0.71073 Å). Powder Xray diffraction patterns were recorded on a Rigaku Miniflex II diffractometer with accelerating voltage and current of 30 kV and 15 mA, respectively. FTIR spectra were obtained on a PerkinElmer Spectrum 100. Raman spectra were measured using a Horiba XploraPLUS Raman spectrometer with diode laser (638 nm) and solid-state laser (473 nm) using a TE Air cooled CCD detector. NMR spectra were collected on Bruker Avance III-HD 300 and Bruker Avance III 400 MHz NMR spectrometers. The 1H and 13C NMR spectra were referenced to natural abundance 13C signals and residual 1 H signals of deuterated solvents, respectively. Thermogravimetric analysis was performed on a SDT Q600 thermogravimetric analyzer using an alumina boat as a sample holder at a heating rate of 5 °C/ min. ICP-MS analysis was conducted using a Finnigan ELEMENT XR double focusing magnetic sector field inductively coupled plasmamass spectrometer (SF-ICP-MS) with Ir, Rh, or both as internal standards. A Micromist U-series nebulizer (0.2 mL/min, GE, Australia), quartz torch, and injector (Thermo Fisher Scientific, USA) were used for sample introduction. Sample gas flow was 1.08 mL/min, and the forwarding power was 1250 W. The samples were

digested in Teflon vessels with nitric and hydrochloric acids and then heated at 180 °C for 4 h. X-ray photoelectron spectroscopy measurements were performed using a Kratos AXIS Ultra DLD XPS system with a monochromatic Al Kα source operated at 15 keV and 150 W and a hemispherical energy analyzer. Samples were placed in small powder pockets on the holder, and analysis was performed at a pressure below 1 × 10−9 mbar. High-resolution core level spectra were measured with a pass energy of 40 eV, and analysis of the data was carried out using XPSPEAK41 software. DR spectra were collected on an Ocean Optics JAZ spectrometer. An Ocean Optics ISP-REF integrating sphere was connected to the spectrometer using a 450 μm SMA fiber optic cable. Samples were loaded in an 8.0 mm quartz sample cell, which was referenced to an Ocean Optics WS-1 Spectralon standard. The conductivity measurements on MOF pressed pellets was performed using a source meter (Keithley Instruments GmbH, Germering, Germany, model 263) and an electrometer (Keithley Instruments GmbH, Germering, Germany, model 617). Theoretical Calculations Methods. The DFT calculations were performed using the Vienna ab initio simulation package (VASP)66,67 with plane wave basis sets. Projector-augmented wave (PAW)68,69 pseudopotentials were employed, with the C 2s22p2, H 1s, O 2s22p4, Th 6s27s26p66d15f1, U 6s27s26p66d25f2, and Co 3d84s1 treated explicitly. The geometries were optimized using the GGA-PBE70 exchange correlation functionals. The van der Waals interactions were taken into account using the dispersion correction formula in the PBE-D3 functionals by Grimme et al.71 with Becke−Johnson damping. In addition, an on-site Coulomb interaction was added to the uranium f-electrons and cobalt d-electrons within the DFT+U formalism72 to attenuate the electron delocalization due to the selfinteraction of electrons. Based on previous studies73,74 a U-J = 4 eV was used for uranium. Although a U-J = 3 eV has been used for cobalt in previous literature,75−77 this value underestimates the experimental band gap of Co containing systems in this work. Thus, a U-J = 4 eV was determined for Co to closely predict the conductivity measurements in this work. No DFT+U corrections are needed for Th, based on previous works78,79 and also confirmed in this work. The planewave energy cutoff was set to 520 eV, and spin-polarized calculations were performed at the Γ-only k-point. Structural optimization was performed until the forces on each ion were less than 25 meV/Å, using 0.0001 eV as the energy tolerance criteria for the electronic step. Gaussian smearing with a width of 0.05 eV was applied to all optimizations. A conjugate-gradient algorithm80,81 was used to relax all the ions. The calculations were performed on SBUs isolated in a cubic box of size 30 Å. The total and partial DOS were calculated by single point calculations following the geometry optimizations.

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ASSOCIATED CONTENT

S Supporting Information *

The Supporting Information is available free of charge on the ACS Publications website at DOI: 10.1021/jacs.9b04737. Additional experimental details, X-ray structure refinement data, PXRD patterns, TGA traces, FTIR, XPS, Tauc plots, 1H NMR spectra and computational details (PDF) Crystallographic information for Th6-Me2BPDC-NO310, CCDC 1910421 (CIF) Crystallographic information for Th6-Me2BPDC-8, CCDC 1910422 (CIF) Crystallographic information for U6-Me2BPDC-TFA-10, CCDC 1910423 (CIF) Crystallographic information for U6-Me2BPDC-8−1dH2O, CCDC 1910424 (CIF) Crystallographic information for U6-Me2BPDC-8−4dH2O, CCDC 1910425 (CIF) Crystallographic information for Th 6 -Me 2 BPDC(Me2TPDC)-12, CCDC 1910426 (CIF) J

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(7) Kalmutzki, M. J.; Hanikel, N.; Yaghi, O. M. Secondary Building Units as the Turning Point in the Development of the Reticular Chemistry of MOFs. Sci. Adv. 2018, 4, 9180−9195. (8) Kalaj, M.; Palomba, J. M.; Bentz, K. C.; Cohen, S. M. Multiple Functional Groups in UiO-66 Improve Chemical Warfare Agent Simulant Degradation. Chem. Commun. 2019, 55, 5367−5370. (9) McGuirk, C.; Oktawiec, J.; Turkiewicz, A.; Taylor, M. K.; Long, J. R. Influence of Metal Substitution on the Pressure-Induced Phase Change in Flexible Zeolitic Imidazolate Frameworks. J. Am. Chem. Soc. 2018, 140, 15924−15933. (10) Feng, M.; Zhang, P.; Zhou, H. C.; Sharma, V. K. Water-Stable Metal-Organic Frameworks for Aqueous Removal of Heavy Metals and Radionuclides: A Review. Chemosphere 2018, 209, 783−800. (11) Ward, A. L.; Buckley, H. L.; Lukens, W. W.; Arnold, J. Synthesis and Characterization of Thorium(IV) and Uranium(IV) Corrole Complexes. J. Am. Chem. Soc. 2013, 135, 13965−13971. (12) Li, Y. L.; Zeidman, B. D.; Hu, S. Y.; Henager, C. H.; Besmann, T. M.; Grandjean, A. A Physics-Based Mesoscale Phase-Field Model for Predicting the Uptake Kinetics of Radionuclides in Hierarchical Nuclear Wasteform Materials. Comput. Mater. Sci. 2019, 159, 103− 109. (13) Le Nedelec, T.; Charlot, A.; Calard, F.; Cuer, F.; Leydier, A.; Grandjean, A. Uranium Adsorption from Sulfuric Acid Media Using Silica Materials Functionalised with Amide and Phosphorous Ligands. New J. Chem. 2018, 42, 14300−14307. (14) Yang, H.; Luo, L.; Wang, H.; Hu, D.; Lin, J.; Wang, X.; Wang, Y.; Wang, S.; Bu, X.; Feng, P.; Wu, T. Highly Selective and Rapid Uptake of Radionuclide Cesium Based on Robust Zeolitic Chalcogenide via Stepwise Ion-Exchange Strategy. Chem. Mater. 2016, 28, 8774−8780. (15) Hendon, C. H.; Rieth, A. J.; Korzyński, M. D.; Dincǎ, M. Grand Challenges and Future Opportunities for Metal-Organic Frameworks. ACS Cent. Sci. 2017, 3, 554−563. (16) Wang, H.; Lustig, W. P.; Li, J. Sensing and Capture of Toxic and Hazardous Gases and Vapors by Metal-Organic Frameworks. Chem. Soc. Rev. 2018, 47, 4729−4756. (17) Yuan, S.; Feng, L.; Wang, K.; Pang, J.; Bosch, M.; Lollar, C.; Sun, Y.; Qin, J.; Yang, X.; Zhang, P.; Wang, Q.; Zou, L.; Zhang, Y.; Zhang, L.; Fang, Y.; Li, J.; Zhou, H.-C. Stable Metal-Organic Frameworks: Design, Synthesis, and Applications. Adv. Mater. 2018, 30, 1704303−1704337. (18) Small, L. J.; Nenoff, T. M. Direct Electrical Detection of Iodine Gas by a Novel Metal−Organic-Framework-Based Sensor. ACS Appl. Mater. Interfaces 2017, 9, 44649−44655. (19) Krause, S.; Bon, V.; Stoeck, U.; Senkovska, I.; Többens, D. M.; Wallacher, D.; Kaskel, S. A Stimuli-Responsive Zirconium Metal− Organic Framework Based on Supermolecular Design. Angew. Chem., Int. Ed. 2017, 56, 10676−10680. (20) Carboni, M.; Abney, C. W.; Liu, S.; Lin, W. Highly Porous and Stable Metal−Organic Frameworks for Uranium Extraction. Chem. Sci. 2013, 4, 2396−2402. (21) Li, P.; Vermeulen, N. A.; Malliakas, C. D.; Gómez-Gualdrón, D. A.; Howarth, A. J.; Mehdi, B. L.; Dohnalkova, A.; Browning, N. D.; O’Keeffe, M.; Farha, O. K. Bottom-up Construction of a Superstructure in a Porous Uranium-Organic Crystal. Science 2017, 356, 624−627. (22) Su, J.; Chen, J. MOFs of Uranium and the Actinides. Struct. Bonding (Berlin, Ger.) 2014, 163, 265−296. (23) Lollar, C. T.; Pang, J.; Qin, J.; Yuan, S.; Powell, J. A.; Zhou, H.C. Thermodynamically Controlled Linker Installation in Flexible Zirconium Metal−Organic Frameworks. Cryst. Growth Des. 2019, 19, 2069−2073. (24) Logan, M. W.; Adamson, J. D.; Le, D.; Uribe-Romo, F. J. Structural Stability of N-Alkyl-Functionalized Titanium Metal− Organic Frameworks in Aqueous and Humid Environments. ACS Appl. Mater. Interfaces 2017, 9, 44529−44533. (25) Khabibullin, A.; Fullwood, E.; Kolbay, P.; Zharov, I. Reversible Assembly of Tunable Nanoporous Materials from “Hairy” Silica Nanoparticles. ACS Appl. Mater. Interfaces 2014, 6, 17306−17312.

Crystallographic information for Th6-Me2BPDC-8-intermediate, CCDC 1910427 (CIF) Crystallographic information for Th 6 -Me 2 BPDC(“QPDC”)-10, CCDC 1910428 (CIF) Crystallographic information for Th 6 -Me 2 BPDC(“Me2BPDC”)-10, CCDC 1910429 (CIF) Crystallographic information for Th6-Me2BPDC-10MeOH, CCDC 1910430 (CIF) Crystallographic information for Th6-BPDC-10, CCDC 1910431 (CIF) Crystallographic information for Th6-BPDC-12, CCDC 1910432 (CIF)

AUTHOR INFORMATION

Corresponding Author

*[email protected] ORCID

Stavros G. Karakalos: 0000-0002-3428-5433 Brian A. Powell: 0000-0003-0423-0180 Hans-Conrad zur Loye: 0000-0001-7351-9098 Kyle S. Brinkman: 0000-0002-2219-1253 Natalia B. Shustova: 0000-0003-3952-1949 Notes

The authors declare no competing financial interest.

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ACKNOWLEDGMENTS This research was supported as part of the Center for Hierarchical Wasteform Materials (CHWM), an Energy Frontier Research Center funded by the U.S. Department of Energy, Office of Science under Award DE-SC0016574. N.B.S. acknowledges the support from the Sloan Research Fellowship provided by Alfred P. Sloan Foundation and Camille Dreyfus Teaching-Scholar Award provided by Henry and Camille Dreyfus Foundation.

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REFERENCES

(1) Schrimpf, W.; Jiang, J.; Ji, Z.; Hirschle, P.; Lamb, D. C.; Yaghi, O. M.; Wuttke, S. Chemical Diversity in a Metal-Organic Framework Revealed by Fluorescence Lifetime Imaging. Nat. Commun. 2018, 9, 1647−1656. (2) Wang, Y.; Liu, Z.; Li, Y.; Bai, Z.; Liu, W.; Wang, Y.; Xu, X.; Xiao, C.; Sheng, D.; Diwu, J.; Su, J.; Chai, Z.; Albrecht-Schmitt, T. E.; Shuao, W. Umbellate Distortions of the Uranyl Coordination Environment Result in a Stable and Porous Polycatenated Framework That Can Effectively Remove Cesium from Aqueous Solutions. J. Am. Chem. Soc. 2015, 137, 6144−6147. (3) Dolgopolova, E. A.; Ejegbavwo, O. A.; Martin, C. R.; Smith, M. D.; Setyawan, W.; Karakalos, S. G.; Henager, C. H.; zur Loye, H.-C.; Shustova, N. B. Multifaceted Modularity: A Key for Stepwise Building of Hierarchical Complexity in Actinide Metal−Organic Frameworks. J. Am. Chem. Soc. 2017, 139, 16852−16861. (4) Li, P.; Vermeulen, N. A.; Gong, X.; Malliakas, C. D.; Stoddart, J. F.; Hupp, J. T.; Farha, O. K. Design and Synthesis of a Water-Stable Anionic Uranium-Based Metal-Organic Framework (MOF) with Ultra Large Pores. Angew. Chem., Int. Ed. 2016, 55, 10358−10362. (5) Furukawa, H.; Cordova, K. E.; O’Keeffe, M.; Yaghi, O. M. The Chemistry and Applications of Metal-Organic Frameworks. Science 2013, 341, 1230444−1230456. (6) Li, P.; Wang, X.; Otake, K.; Lyu, J.; Hanna, S. L.; Islamoglu, T.; Farha, O. K. Synthetic Control of Thorium Polyoxo-Clusters in Metal−Organic Frameworks toward New Thorium-Based Materials. ACS Appl. Nano Mater. 2019, 2, 2260−2265. K

DOI: 10.1021/jacs.9b04737 J. Am. Chem. Soc. XXXX, XXX, XXX−XXX

Article

Journal of the American Chemical Society (26) Pattengale, B.; SantaLucia, D. J.; Yang, S.; Hu, W.; Liu, C.; Zhang, X.; Berry, J. F.; Huang, J. Direct Observation of Node-to-Node Communication in Zeolitic Imidazolate Frameworks. J. Am. Chem. Soc. 2018, 140, 11573−11576. (27) Xia, Z.; Poeppelmeier, K. R. Chemistry-Inspired Adaptable Framework Structures. Acc. Chem. Res. 2017, 50, 1222−1230. (28) Zhang, Y.; Zhang, X.; Lyu, J.; Otake, K.-I.; Wang, X.; Redfern, L. R.; Malliakas, C. D.; Li, Z.; Islamoglu, T.; Wang, B.; Farha, O. K. A Flexible Metal-Organic Framework with 4-Connected Zr6 Nodes. J. Am. Chem. Soc. 2018, 140, 11179−11183. (29) Martin, N. P.; März, J.; Feuchter, H.; Duval, S.; Roussel, P.; Henry, N.; Ikeda-Ohno, A.; Loiseau, T.; Volkringer, C. Synthesis and Structural Characterization of the First Neptunium Based MetalOrganic Frameworks Incorporating {Np6O8} Hexanuclear Clusters. Chem. Commun. 2018, 54, 6979−6982. (30) Cavka, J. H.; Jakobsen, S.; Olsbye, U.; Guillou, N.; Lamberti, C.; Bordiga, S.; Lillerud, K. P. A New Zirconium Inorganic Building Brick Forming Metal Organic Frameworks with Exceptional Stability. J. Am. Chem. Soc. 2008, 130, 13850−13851. (31) Wang, H.; Dong, X.; Lin, J.; Teat, S. J.; Jensen, S.; Cure, J.; Alexandrov, E. V.; Xia, Q.; Tan, K.; Wang, Q.; Olson, D. H.; Proserpio, D. M.; Chabal, Y. J.; Thonhauser, T.; Sun, J.; Han, Y.; Li, J. Topologically Guided Tuning of Zr-MOF Pore Structures for Highly Selective Separation of C6 Alkane Isomers. Nat. Commun. 2018, 9, 1745−1755. (32) Bueken, B.; Vermoortele, F.; Cliffe, M. J.; Wharmby, M. T.; Foucher, D.; Wieme, J.; Vanduyfhuys, L.; Martineau, C.; Stock, N.; Taulelle, F.; Van Speybroeck, V.; Goodwin, A. L.; De Vos, D. A Breathing Zirconium Metal-Organic Framework with Reversible Loss of Crystallinity by Correlated Nanodomain Formation. Chem. - Eur. J. 2016, 22, 3264−3267. (33) Deria, P.; Gómez-Gualdrón, D. A.; Bury, W.; Schaef, H. T.; Wang, T. C.; Thallapally, P. K.; Sarjeant, A. A.; Snurr, R. Q.; Hupp, J. T.; Farha, O. K. Ultraporous, Water Stable, and Breathing ZirconiumBased Metal-Organic Frameworks with Ftw Topology. J. Am. Chem. Soc. 2015, 137, 13183−13190. (34) Furukawa, H.; Gándara, F.; Zhang, Y.-B.; Jiang, J.; Queen, W. L.; Hudson, M. R.; Yaghi, O. M. Water Adsorption in Porous Metal− Organic Frameworks and Related Materials. J. Am. Chem. Soc. 2014, 136, 4369−4381. (35) Souza, B. E.; Rudić, S.; Titov, K.; Babal, A. S.; Taylor, J. D.; Tan, J.-C. Guest−Host Interactions of Nanoconfined Anti-Cancer Drug in Metal−Organic Framework Exposed by Terahertz Dynamics. Chem. Commun. 2019, 55, 3868−3871. (36) Devic, T.; Horcajada, P.; Serre, C.; Salles, F.; Maurin, G.; Moulin, B.; Heurtaux, D.; Clet, G.; Vimont, A.; Grenéche, J. M.; Le Ouay, B.; Moreau, F.; Magnier, E.; Filinchuk, Y.; Marrot, J.; Lavalley, J.; Daturi, M.; Férey, G. Functionalization in Flexible Porous Solids: Effects on the Pore Opening and the Host-Guest Interactions. J. Am. Chem. Soc. 2010, 132, 1127−1136. (37) Lee, S.; Bürgi, H. B.; Alshmimri, S. A.; Yaghi, O. M. Impact of Disordered Guest-Framework Interactions on the Crystallography of Metal-Organic Frameworks. J. Am. Chem. Soc. 2018, 140, 8958−8964. (38) Bhunia, M. K.; Hughes, J. T.; Fettinger, J. C.; Navrotsky, A. Thermochemistry of Paddle Wheel MOFs: Cu-HKUST-1 and ZnHKUST-1. Langmuir 2013, 29, 8140−8145. (39) Joback, K. G.; Reid, R. C. Estimation of Pure-Component Properties from Group-Contributions. Chem. Eng. Commun. 1987, 57, 233−243. (40) OECD/NEA (2008), Chemical Thermodynamics of Thorium, Chemical Thermodynamics, OECD Publishing, Paris. (41) Robie, R. A.; Hemingway, B. S. Thermodynamic Properties of Minerals and Related Substances at 298.15 K and 1 bar (105 Pascals) Pressure and at Higher Temperatures; Washington, 1995. (42) Vasil’eva, T. F.; Zhil’tsova, E. N.; Vvedenskii, A. A. Enthalpies of Combustion of NN-Dimethylformamide and NN-Dimethylacetamide. Russ. J. Phys. Chem. (Engl. Transl.) 1972, 46, 315.

(43) Hughes, J. T.; Navrotsky, A. MOF-5: Enthalpy of Formation and Energy Landscape of Porous Materials. J. Am. Chem. Soc. 2011, 133, 9184−9187. (44) Akimbekov, Z.; Wu, D.; Brozek, C. K.; Dincǎ, M.; Navrotsky, A. Thermodynamics of Solvent Interaction with the Metal−Organic Framework MOF-5. Phys. Chem. Chem. Phys. 2016, 18, 1158−1162. (45) Bureekaew, S.; Amirjalayer, S.; Schmid, R. Orbital Directing Effects in Copper and Zinc Based Paddle-Wheel Metal Organic Frameworks: The Origin of Flexibility. J. Mater. Chem. 2012, 22, 10249−10254. (46) Hughes, J. T.; Bennett, T. D.; Cheetham, A. K.; Navrotsky, A. Thermochemistry of Zeolitic Imidazolate Frameworks of Varying Porosity. J. Am. Chem. Soc. 2013, 135, 598−601. (47) Yuan, S.; Chen, Y.-P.; Qin, J.-S.; Lu, W.; Wang, X.; Zhang, Q.; Bosch, M.; Liu, T.-F.; Lian, X.; Zhou, H.-C. Cooperative Cluster Metalation and Ligand Migration in Zirconium Metal-Organic Frameworks. Angew. Chem., Int. Ed. 2015, 54, 14696−14700. (48) Falaise, C.; Delille, J.; Volkringer, C.; Vezin, H.; Rabu, P.; Loiseau, T. Series of Hydrated Heterometallic Uranyl-Cobalt(II) Coordination Polymers with Aromatic Polycarboxylate Ligands: Formation of UO−Co Bonding upon Dehydration Process. Inorg. Chem. 2016, 55, 10453−10466. (49) Schneemann, A.; Bon, V.; Schwedler, I.; Senkovska, I.; Kaskel, S.; Fischer, R. A. Flexible Metal-Organic Frameworks. Chem. Soc. Rev. 2014, 43, 6062−6096. (50) Chen, C. X.; Wei, Z.; Jiang, J. J.; Fan, Y. Z.; Zheng, S. P.; Cao, C. C.; Li, Y. H.; Fenske, D.; Su, C. Y. Precise Modulation of the Breathing Behavior and Pore Surface in Zr-MOFs by Reversible PostSynthetic Variable-Spacer Installation to Fine-Tune the Expansion Magnitude and Sorption Properties. Angew. Chem., Int. Ed. 2016, 55, 9932−9936. (51) Schaate, A.; Roy, P.; Godt, A.; Lippke, J.; Waltz, F.; Wiebcke, M.; Behrens, P. Modulated Synthesis of Zr-Based Metal-Organic Frameworks: From Nano to Single Crystals. Chem. - Eur. J. 2011, 17, 6643−6651. (52) Yuan, S.; Lu, W.; Chen, Y.-P.; Zhang, Q.; Liu, T.-F.; Feng, D.; Wang, X.; Qin, J.-S.; Zhou, H.-C. Sequential Linker Installation: Precise Placement of Functional Groups in Multivariate MetalOrganic Frameworks. J. Am. Chem. Soc. 2015, 137, 3177−3180. (53) Halder, A.; Ghoshal, D. Structure and Properties of Dynamic Metal-Organic Frameworks: A Brief Accounts of Crystalline-toCrystalline and Crystalline-to-Amorphous Transformations. CrystEngComm 2018, 20, 1322−1345. (54) Helal, A.; Yamani, Z. H.; Cordova, K. E.; Yaghi, O. M. Multivariate Metal-Organic Frameworks. Natl. Sci. Rev. 2017, 4, 296− 298. (55) Zhang, Y. B.; Furukawa, H.; Ko, N.; Nie, W.; Park, H. J.; Okajima, S.; Cordova, K. E.; Deng, H.; Kim, J.; Yaghi, O. M. Introduction of Functionality, Selection of Topology, and Enhancement of Gas Adsorption in Multivariate Metal-Organic Framework177. J. Am. Chem. Soc. 2015, 137, 2641−2650. (56) Chen, W.; Zhang, P.; Zhou, H.-C.; Drake, H. F.; Zhang, L.; Yuan, S.; Sokaras, D.; Day, G. S.; Feng, L.; Elumalai, P.; Madrahimov, S. T.; Sun, D.; Qun, J.-S.; Garcia-Esparza, A. T. Exposed Equatorial Positions of Metal Centers via Sequential Ligand Elimination and Installation in MOFs. J. Am. Chem. Soc. 2018, 140, 10814−10819. (57) Yuan, S.; Chen, Y. P.; Qin, J. S.; Lu, W.; Zou, L.; Zhang, Q.; Wang, X.; Sun, X.; Zhou, H. C. Linker Installation: Engineering Pore Environment with Precisely Placed Functionalities in Zirconium MOFs. J. Am. Chem. Soc. 2016, 138, 8912−8919. (58) Cao, C. C.; Chen, C. X.; Wei, Z. W.; Qiu, Q. F.; Zhu, N. X.; Xiong, Y. Y.; Jiang, J. J.; Wang, D.; Su, C. Y. Catalysis through Dynamic Spacer Installation of Multivariate Functionalities in MetalOrganic Frameworks. J. Am. Chem. Soc. 2019, 141, 2589−2593. (59) Luo, T. Y.; Liu, C.; Gan, X. Y.; Muldoon, P. F.; Diemler, N. A.; Millstone, J. E.; Rosi, N. L. Multivariate Stratified Metal-Organic Frameworks: Diversification Using Domain Building Blocks. J. Am. Chem. Soc. 2019, 141, 2161−2168. L

DOI: 10.1021/jacs.9b04737 J. Am. Chem. Soc. XXXX, XXX, XXX−XXX

Article

Journal of the American Chemical Society

Adatoms on the Major Surfaces of Thorium Dioxide. J. Nucl. Mater. 2016, 473, 99−111. (79) Pegg, J. T.; Aparicio-Anglès, X.; Storr, M.; de Leeuw, N. H. DFT+U Study of the Structures and Properties of the Actinide Dioxides. J. Nucl. Mater. 2017, 492, 269−278. (80) Bylander, D. M.; Kleinman, L.; Lee, S. Self-Consistent Calculations of the Energy Bands and Bonding Properties of B 12 C 3. Phys. Rev. B: Condens. Matter Mater. Phys. 1990, 42, 1394−1403. (81) Teter, M. P.; Payne, M. C.; Allan, D. C. Solution of Schrödinger’s Equation for Large Systems. Phys. Rev. B: Condens. Matter Mater. Phys. 1989, 40, 12255−12263.

(60) Zur Loye, H. C.; Besmann, T.; Amoroso, J.; Brinkman, K.; Grandjean, A.; Henager, C. H.; Hu, S.; Misture, S. T.; Phillpot, S. R.; Shustova, N. B.; Wang, H.; Koch, R.; Morrison, G.; Dolgopolova, E. Hierarchical Materials as Tailored Nuclear Waste Forms: A Perspective. Chem. Mater. 2018, 30, 4475−4488. (61) Hu, P.; Yin, L.; Kirchon, A.; Li, J.; Li, B.; Wang, Z.; Ouyang, Z.; Zhang, T.; Zhou, H.-C. Magnetic Metal−Organic Framework Exhibiting Quick and Selective Solvatochromic Behavior along with Reversible Crystal-to-Amorphous-to-Crystal Transformation. Inorg. Chem. 2018, 57, 7006−7014. (62) Deng, M.; Pan, Y.; Zhu, J.; Chen, Z.; Sun, Z.; Sun, J.; Ling, Y.; Zhou, Y.; Feng, P. Cation-Exchange Approach to Tuning the Flexibility of a Metal−Organic Framework for Gated Adsorption. Inorg. Chem. 2017, 56, 5069−5075. (63) Burrows, A. D.; Frost, C. G.; Mahon, M. F.; Richardson, C. Sulfur-Tagged Metal-Organic Frameworks and Their Post-Synthetic Oxidation. Chem. Commun. 2009, 0, 4218−4220. (64) Bowen, A. M.; Jones, M. W.; Lovett, J. E.; Gaule, T. G.; McPherson, M. J.; Dilworth, J. R.; Timmel, C. R.; Harmer, J. R. Exploiting Orientation-Selective DEER: Determining Molecular Structure in Systems Containing Cu(II) Centres. Phys. Chem. Chem. Phys. 2016, 18, 5981−5994. (65) Hylland, K.; Øien-Ødegaard, S.; Lillerud, K.; Tilset, M. Efficient, Scalable Syntheses of Linker Molecules for Metal-Organic Frameworks. Synlett 2015, 26, 1480−1485. (66) Kresse, G.; Hafner, J. Ab Initio Molecular Dynamics for Liquid Metals. Phys. Rev. B: Condens. Matter Mater. Phys. 1993, 47, 558−561. (67) Kresse, G.; Furthmüller, J. Efficient Iterative Schemes for Ab Initio Total-Energy Calculations Using a Plane-Wave Basis Set. Phys. Rev. B: Condens. Matter Mater. Phys. 1996, 54, 11169−11186. (68) Blöchl, P. E. Projector Augmented-Wave Method. Phys. Rev. B: Condens. Matter Mater. Phys. 1994, 50, 17953−17979. (69) Kresse, G.; Joubert, D. From Ultrasoft Pseudopotentials to the Projector Augmented-Wave Method. Phys. Rev. B: Condens. Matter Mater. Phys. 1999, 59, 1758−1775. (70) Perdew, J. P.; Burke, K.; Ernzerhof, M. Generalized Gradient Approximation Made Simple. Phys. Rev. Lett. 1996, 77, 3865−3868. (71) Grimme, S.; Antony, J.; Ehrlich, S.; Krieg, H. A Consistent and Accurate Ab Initio Parametrization of Density Functional Dispersion Correction (DFT-D) for the 94 Elements H-Pu. J. Chem. Phys. 2010, 132, 154104−154122. (72) Dudarev, S. L.; Botton, G. A.; Savrasov, S. Y.; Humphreys, C. J.; Sutton, A. P. Electron-Energy-Loss Spectra and the Structural Stability of Nickel Oxide: An LSDA+U Study. Phys. Rev. B: Condens. Matter Mater. Phys. 1998, 57, 1505−1509. (73) Dorado, B.; Amadon, B.; Freyss, M.; Bertolus, M. DFT+U Calculations of the Ground State and Metastable States of Uranium Dioxide. Phys. Rev. B: Condens. Matter Mater. Phys. 2009, 79, 235125−235132. (74) Dudarev, S. L.; Castell, M. R.; Botton, G. A.; Savrasov, S. Y.; Muggelberg, C.; Briggs, G. A. D.; Sutton, A. P.; Goddard, D. T. Understanding STM Images and EELS Spectra of Oxides with Strongly Correlated Electrons: A Comparison of Nickel and Uranium Oxides. Micron 2000, 31, 363−372. (75) Ritzmann, A. M.; Pavone, M.; Muñoz-García, A. B.; Keith, J. A.; Carter, E. A. Ab Initio DFT+U Analysis of Oxygen Transport in LaCoO 3: The Effect of Co 3+ Magnetic States. J. Mater. Chem. A 2014, 2, 8060−8074. (76) Zhang, S.; Han, N.; Tan, X. Density Functional Theory Calculations of Atomic, Electronic and Thermodynamic Properties of Cubic LaCoO3 and La1−xSrxCoO3 Surfaces. RSC Adv. 2015, 5, 760− 769. (77) Olsson, E.; Aparicio-Anglès, X.; De Leeuw, N. H. Ab Initio Study of Vacancy Formation in Cubic LaMnO3 and SmCoO3 as Cathode Materials in Solid Oxide Fuel Cells. J. Chem. Phys. 2016, 145, 014703−014712. (78) Shields, A. E.; Santos-Carballal, D.; De Leeuw, N. H. A Density Functional Theory Study of Uranium-Doped Thoria and Uranium M

DOI: 10.1021/jacs.9b04737 J. Am. Chem. Soc. XXXX, XXX, XXX−XXX